CN107002204B - Oriented electrical steel and its manufacturing method - Google Patents
Oriented electrical steel and its manufacturing method Download PDFInfo
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- CN107002204B CN107002204B CN201480084060.4A CN201480084060A CN107002204B CN 107002204 B CN107002204 B CN 107002204B CN 201480084060 A CN201480084060 A CN 201480084060A CN 107002204 B CN107002204 B CN 107002204B
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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Abstract
The oriented electrical steel of one embodiment of the invention, Ba individually includes that perhaps Y individually includes that 0.005 weight % to 0.5 weight % or Ba and Y jointly comprises 0.005% to 0.5% to 0.005 weight % to 0.5 weight % in base steel sheet, and surplus includes Fe and impurity.
Description
Technical field
The present invention relates to a kind of oriented electrical steel and its manufacturing methods.
Background technique
Typically for the outstanding oriented electrical steel of magnetic property, the Goss texture (Goss of { 110 }<001>orientation
Texture) should be highly developed along steel plate rolling direction, it, need to be excrescent 2 times by crystal grain in order to form such texture
Recrystallization is orientated crystal grain to form Gauss.
It is in normal grain growth because of precipitate, folder that this improper crystalline growth, which is different from conventional grain growth,
When the element of sundries or solid solution or cyrystal boundary segregation and the crystal boundary migration by normal growth are suppressed.
Oriented electrical steel, which is mainly employed as grain growth inhibitor, causes 2 times using precipitates such as AlN, MnS again
The manufacturing method of crystallization.This oriented electrical steel board fabrication method that AlN, MnS precipitate are used as grain growth inhibitor is deposited
In following problem.
In order to which AlN, MnS precipitate are used as grain growth inhibitor, need to keep precipitate very fine and equably divide
Cloth is in steel plate.
In this way, needing slab to be evenly distributed fine precipitate with 1300 DEG C or more of high temperature long-time
Heating, so that after the solid solution of coarse precipitates present in steel, and implement hot rolling within the very fast time, not to be precipitated
In the state of terminate hot rolling.
Large-scale veneer heating apparatus is needed thus, and in order to inhibit to be precipitated to the maximum extent, is needed very strict
Ground manages hot rolling and coiling technique, it is also necessary to fine by managing the precipitate being dissolved in the hot rolled plate annealing process after making hot rolling
It is precipitated.
In addition, by slab to be heated at high temperature when, due to formed low melting point Fe2SiO4, therefore generate plate and wash (washing)
Phenomenon, so as to cause decrease in yield.
In addition, in order to remove precipitate component, needing to carry out 30 at a high temperature of 1200 DEG C after 2 recrystallizations
Hour or more long-time purify annealing, therefore there are problems that brought by the complexity in manufacturing process and cost burden.
Moreover, for AlN precipitate after resolving into Al and N, Al can move to surface of steel plate in this purification annealing process
It is reacted with the oxygen of surface oxide layer, thus forms Al2O3Oxide.
Undecomposed AlN precipitate is in steel plate or surface in the Al base oxide that is thusly-formed or purification annealing process
The movement of magnetic domain is nearby interfered, to become the reason of causing iron loss to deteriorate.
Summary of the invention
(1) technical problems to be solved
One embodiment of the invention provides a kind of oriented electrical steel.
Another embodiment of the present invention provides a kind of manufacturing methods of oriented electrical steel.
(2) technical solution
The oriented electrical steel of an exemplary implementation scheme of the invention, Ba individually includes 0.005 in base steel sheet
Weight % to 0.5 weight % or Y individually include that 0.005 weight % to 0.5 weight % or Ba and Y jointly comprises 0.005%
To 0.5%, surplus includes Fe and impurity.
It also may include that Si:1.0% to 7.0%, C:0.0050% or less (do not include in terms of weight % in the base steel sheet
0%), Al:0.005% or less (not including 0%), N:0.0055% or less (not including 0%), S:0.0055% or less (are not wrapped
0%) and Mn:0.01% to 0.5% it includes.
In the electric steel plate, the area ratio of the crystal grain with 2mm or less partial size can be 10% or less.
In the electric steel plate, the average grain diameter of the crystal grain with 2mm or more partial size can be 10mm or more.
In addition, in the electric steel plate, the plate face of<100>face and steel plate be formed by angle difference can for 3.5 ° with
Under.
In the steel plate, the magnetic flux density B that is measured under the magnetic field of 1000A/m10It can be 1.88 or more.
The electric steel plate may include Ba, the Y or their combination for segregating to crystal boundary.
The manufacturing method of the oriented electrical steel of an exemplary implementation scheme of the invention includes: to heat to slab
The step of, in the slab Ba individually include 0.005 weight % to 0.5 weight % or Y individually include 0.005 weight % extremely
0.5 weight % or Ba and Y jointly comprises 0.005% to 0.5%, and surplus includes Fe and other inevitable impurity；To institute
It states slab and carries out the step of hot rolling is to manufacture hot rolled plate；The step of cold rolling is to manufacture cold-reduced sheet is carried out to the hot rolled plate；To institute
State the step of cold-reduced sheet carries out 1 recrystallization annealing；And the electric steel plate that 1 recrystallization annealing finishes tie again for 2 times
The step of crystalline substance annealing.
The slab also may include Si:1.0% to 4.5%, C:0.001% in terms of weight % to 0.1%, Al:0.005%
Below, N:0.0055% or less, S:0.0055% or less and Mn:0.01% to 0.5%.
Slab heating temperature can be 1280 DEG C or less in described the step of heating to slab.
Soaking temperature can be 900 DEG C to 1250 DEG C when 2 recrystallization annealing.
After the hot-rolled step, it may also include the step of implementing hot rolled plate annealing.
In 1 recrystallization annealing can by cold-reduced sheet 750 DEG C or more at a temperature of kept for 30 seconds or more.
(3) beneficial effect
The oriented electrical steel of one embodiment of the invention is stably formed Gauss crystal grain, thus iron loss is low and magnetic property is excellent
It is elegant.
In addition, AlN and MnS is not used as grain growth inhibitor, because without at a high temperature of 1300 DEG C or more
Carry out slab reheating.
Also, it is not necessary to carry out for removing the precipitates such as AlN and MnS high temperature purification annealing, thus save manufacture at
This.
In addition, due to not needing to remove N and S etc. after the high-temperature anneal, because the gas of N, S in purification annealing process may be not present
Change surface defect caused by reaction.
Specific embodiment
Advantages of the present invention, feature and the side for realizing these can be expressly understood referring to attached drawing and following embodiments
Method.However, the present invention can be implemented in a variety of ways, it is not limited to embodiment disclosed below.Following realities are provided
The purpose for applying example is, the sufficiently open present invention so that those skilled in the art have to summary of the invention it is whole and sufficient
Solution, protection scope of the present invention should be subject to claims.Identical appended drawing reference indicates identical structure in specification in the whole text
At element.
Therefore, in some embodiments, widely-known technique is repeated no more, is explained fuzzy to avoid the present invention
It is unclear.Unless otherwise defined, the meaning of all terms (including technical terms and scientific terms) used in this specification
It is exactly the normally understood meaning of those skilled in the art.In specification in the whole text, certain a part " including (or comprising) " certain
When one constituent element, unless there are especially opposite record, otherwise indicate can also to include other constituent elements and it is non-excluded other
Structure element.Unless otherwise stated, singular is also intended to including plural form.
In addition, % indicates that weight %, 1ppm are 0.0001 weight % in the case where being not specifically mentioned.
The manufacturing method of the oriented electrical steel of an exemplary implementation scheme of the invention is illustrated below.
Slab is provided, it individually includes 0.005 that Ba, which individually includes 0.005 weight % to 0.5 weight % or Y, in the slab
Weight % to 0.5 weight % or Ba and Y jointly comprises 0.005% to 0.5%, and surplus includes Fe and other are inevitably miscellaneous
Matter.
The slab also may include in terms of weight % Si:1.0% to 4.5%, C:0.005% or less, Al:0.005% with
Under, N:0.0055% or less, S:0.0055% or less and Mn:0.01% to 0.5%.
Illustrate the reasons why limiting ingredient first.
Ba and Y play the role of grain growth inhibitor, inhibit other except Gauss crystal grain in 2 recrystallization annealing
It is orientated the growth of crystal grain, to improve the magnetism of electric steel plate.Ba and Y can be individually added into respectively or be added jointly, content
When less than 0.005%, it is difficult to which when playing sufficient restraint, and being greater than 0.5%, the brittleness of steel plate be will increase, it is possible to cause
It is cracked when rolling.
Si plays the role of increasing the resistivity of material to reduce iron loss.Si content is less than in slab and electric steel plate
When 1.0%, resistivity reduces, it is possible to core loss property be caused to decline.In addition, when the Si content in slab is greater than 4.5%, cold rolling
It can become difficult.But after cold rolling, can by the surface of Si powder coating to steel plate or deposition make afterwards on a surface of a steel sheet
Si is diffused into the inside of steel plate, therefore the content of Si can be 4.5% or more in the electric steel plate of final material.However, if
Si content is greater than 7% in oriented electrical steel, then is difficult to when manufacturing transformer, therefore the Si in oriented electrical steel contains
Amount can be 7% or less.
C is among the austenite stabilizing elements, 0.001% or more is added in slab, so that the coarse column generated in continuous casting process
Structure refinement can also inhibit the central segregation of slab of S.Moreover, promoting the processing hardening of steel plate in cold rolling, thus can be with
Promote 2 recrystallizations nucleation of { 110 }<001>orientation in steel plate.However, side can be generated in hot rolling when C content is greater than 0.1%
Marginal slit line (edge-crack).But pass through decarburizing annealing when manufacturing electric steel plate, C content can be 0.0050 weight after decarburizing annealing
Measure % or less.More specifically, can be 0.0030 weight % or less.
In an embodiment of the present invention, AlN can not be used as grain growth inhibitor, thus can effectively inhibits Al
Content.Therefore, in an embodiment of the present invention, Al will not be added into or can control below 0.005%.
N will form AlN, (Al, Mn) N, (Al, Si, Mn) N, Si3N4Deng precipitation, therefore N will not in one embodiment of the invention
It is added into or may be controlled to 0.0055% or less.It specifically, can be 0.0035% or less.More specifically, can be
0.0015% or less.
Solid solubility temperature is high when S is hot rolling and the serious element of segregation, thus can be added without in one embodiment of the invention or
Person's control is 0.0055% or less.It specifically, can be 0.0035% or less.More specifically, can be 0.0015% or less.
In an exemplary implementation scheme of the invention, MnS is not used as grain growth inhibitor, therefore can not
Mn is added.But Mn has the effect of that magnetism can be improved as resistivity element, therefore the Mn content in slab and electric steel plate
It can be 0.01% or more.However, when Mn content is greater than 0.5% phase transformation can be caused after 2 recrystallizations, it is possible to leading to magnetic
Property be deteriorated.
The ingredients such as Ti, Mg, Ca are reacted with oxygen in steel and form oxide, are preferably added without.But, it is contemplated that in steel
Impurity, can be controlled in 0.005% or less respectively.
The slab is heated.The heating temperature of slab is unrestricted, but to slab with 1280 DEG C of temperature below
When being heated, can avoid slab column crystallization tissue growth obtain it is coarse, to prevent from cracking in hot rolling technology.Cause
This, the heating temperature of slab can be 1000 DEG C or more and 1280 DEG C or less.
Hot rolling is carried out after the reheating of slab.Hot-rolled temperature or cooling temperature are unrestricted, can be in an embodiment
Terminate hot rolling at 950 DEG C of temperature below, can be batched at 600 DEG C of temperature below after water cooling.
Hot rolled plate after hot rolling can implement hot rolled plate annealing as needed or not firm hot rolled plate of applying is annealed, then carry out cold
It rolls.When implementing hot rolled plate annealing, in order to keep hot rolling microstructure uniform, after can realizing soaking with 900 DEG C or more of temperature heating, then
It is cooled down.
Cold rolling can utilize reversible (Reverse) milling train or tandem (Tandom) milling train, by including 1 cold rolling, more
The cold-reduced sheet of the multiple cold-rolling practice of secondary cold rolling or intermediate annealing manufacture 0.1mm to 0.5mm.
In addition, the implementable warm-rolling that steel billet temperature is maintained to 100 DEG C or more in cold rolling.Moreover, cold rolling can be cold by 1 time
Rolling causes the final thickness of 0.1mm to 0.5mm.
1 recrystallization annealing is carried out to the steel plate that cold rolling finishes.Decarburization and Gauss crystal grain occur in 1 recrystallization annealing
1 recrystallization of nucleation.
In 1 recrystallization annealing can by cold-reduced sheet 750 DEG C or more at a temperature of kept for 30 seconds or more.Temperature is lower than
At 750 DEG C, the sufficient energy for grain growth can not be provided, and when the time is shorter than 30 seconds, grain growth is insufficient, from
And it is likely to result in magnetic decline.
In addition, in the manufacturing method of the oriented electrical steel of an exemplary implementation scheme of the invention, decarburizing annealing
After can be omitted nitridation annealing process.It is used as the manufacturing method of the oriented electrical steel of grain growth inhibitor in existing AlN
In, it needs to carry out nitridation annealing to form AlN.However, the manufacturer of the oriented electrical steel in one embodiment of the invention
In method, AlN is not used as grain growth inhibitor, therefore does not need nitridation annealing process.
The steel plate coating that 1 recrystallization annealing finishes includes the annealing separating agent of MgO, then implements 2 recrystallization annealing.Institute
Soaking temperature can be 900 DEG C to 1250 DEG C when stating 2 recrystallization annealing.When temperature is lower than 900 DEG C, Gauss crystal grain will not sufficiently be given birth to
It is long, it is possible to reduce it is magnetic, and when temperature is higher than 1250 DEG C, grain growth obtain it is coarse, it is possible to reducing electrical sheet
The performance of plate.
In the manufacturing method of the oriented electrical steel of one embodiment of the invention, it can be saved after 2 recrystallization annealing
Slightly purify annealing process.
In the manufacturing method that existing MnS, AlN are used as the oriented electrical steel of grain growth inhibitor, in order to remove
The precipitates such as AlN and MnS need to carry out high temperature purification annealing, but the manufacturer of the oriented electrical steel of one embodiment of the invention
Purification annealing process is not needed in method.
For the oriented electrical steel of one embodiment of the invention, Ba individually includes 0.005 weight % to 0.5 in base steel sheet
Weight % or Y individually include that 0.005 weight % to 0.5 weight % or Ba and Y jointly comprises 0.005% to 0.5%, surplus
Include Fe and impurity.Base steel sheet refers to the part except the coating being formed in oriented electrical steel plate surface.
Moreover, also may include in terms of weight % in the base steel sheet Si:1.0% to 7.0%, C:0.005% or less,
Al:0.005% or less, N:0.0055% or less, S:0.0055% or less and Mn:0.01% are to 0.5%.
In addition, Ba, Y or their combination may include 0.02% to 0.35%.
In addition, in the electric steel plate, relative to total chip area 100%, the face of the crystal grain with 2mm or less partial size
Product ratio can be 10% or less.Area ratio relative to total chip area 100%, the crystal grain with 2mm or less partial size is greater than
When 10%, crystal grain is not sufficiently grown, it is possible to reducing magnetic.
In addition, the average grain diameter of the crystal grain with 2mm or more partial size can be 10mm or more in the electric steel plate.Tool
When having the average grain diameter of the crystal grain of 2mm or more partial size to be less than 10mm, crystal grain is not sufficiently grown, it is possible to reducing magnetic.
In addition, in the electric steel plate, the plate face of<100>face and steel plate be formed by angle difference can for 3.5 ° with
Under.The rolling direction of steel plate is set to X-axis and when width direction is set to Y-axis, and the plate face of steel plate refers to the face XY.When being greater than 3.5 °,
The magnetism of steel plate can reduce.
In addition, the magnetic flux density B10 measured under the magnetic field of 1000A/m in the steel plate can be 1.88 or more.Moreover, institute
It states Ba, Y or their combination plays the role of inhibitor, crystal boundary may be segregated to.
It is described in detail below by embodiment.But following embodiments are examples of the invention, and the contents of the present invention are not
It is limited to following embodiments.
[embodiment 1]
Prepare slab, the slab includes Si:3.2%, C:0.051%, Mn:0.112%, S in terms of weight %:
0.0052%, N:0.005% and Al:0.0029%, and include barium (Ba) and yttrium (Y), surplus with content as shown in Table 1
It is made of Fe and other inevitable mixed impurity.
By the slab 1150 DEG C at a temperature of heating 90 minutes after carry out hot rolling, to manufacture with a thickness of 2.6mm
Hot rolled plate.It is kept for 90 seconds at 910 DEG C after the hot rolled plate is heated with 1050 DEG C or more of temperature, then after carrying out water cooling
Pickling.Then, it is cold rolled to a thickness of 0.29mm.After the steel plate of cold rolling heats up in furnace, in hydrogen (50 volume %) and nitrogen (50 bodies
Product %) mixed gas protected lower and 60 DEG C of dew-point temperature and 850 DEG C of annealing temperature under is kept for 120 seconds to carry out 1 time
Recrystallization annealing.After 1 recrystallization annealing, carbon is 0.0030 weight %.Then, coiled material shape is coiled into after coating MgO, and is carried out
2 recrystallization annealing.
Final annealing be nitrogen (25 volume %) and hydrogen (75 volume %) it is mixed gas protected under be warming up to 1200 DEG C, temperature
After degree reaches 1200 DEG C, keep cooling in 20 hours carry out furnaces under hydrogen (100 volume %) protection.
[table 1]
As can be recognized from Table 1, the content of Ba and Y is controlled into the invention material in 0.005% to 0.5% range of the invention
Magnetism be better than contrast material.
[embodiment 2]
Prepare slab, the slab includes Si:3.2%, C:0.051%, Mn:0.112%, S in terms of weight %:
0.0052%, N:0.005% and Al:0.0029%, and include barium (Ba) and yttrium (Y), surplus with content as shown in Table 2
It is made of Fe and other inevitable impurity.
By the slab 1150 DEG C at a temperature of heating 90 minutes after carry out hot rolling, to manufacture with a thickness of 2.6mm
Hot rolled plate.It is kept for 90 seconds at 910 DEG C after the hot rolled plate is heated with 1050 DEG C or more of temperature, then after carrying out water cooling
Pickling.Then, it is cold rolled to a thickness of 0.29mm.After the steel plate of cold rolling heats up in furnace, in hydrogen (50 volume %) and nitrogen (50 bodies
Product %) mixed gas protected lower and 60 DEG C of dew-point temperature and 850 DEG C of annealing temperature under is kept for 120 seconds to carry out 1 time
Recrystallization annealing.After 1 recrystallization annealing, carbon is 0.0030 weight %.Then, coiled material shape is coiled into after coating MgO, and is carried out
2 recrystallization annealing.
Final annealing be nitrogen (25 volume %) and hydrogen (75 volume %) it is mixed gas protected under be warming up to 1200 DEG C, temperature
After degree reaches 1200 DEG C, keep cooling in 20 hours carry out furnaces under hydrogen (100 volume %) protection.
[table 2]
Table 3 is referred to, size is the area ratio of 1mm crystal grain below in the electric steel plate of one embodiment of the invention
(%) is shown as 10% hereinafter, the mean size that size is the crystal grain of 1mm or more is shown as 10mm or more.
The embodiment of the present invention is illustrated above by reference to attached drawing, but those skilled in the art is appreciated that
In the case where not changing technical idea and essential feature, the present invention can be implemented with other specific embodiments.
Therefore, above-described embodiment is only exemplary not restrictive.Protection scope of the present invention should be with claim
Subject to book rather than above description, have altered or change as derived from the meaning, range and such equivalents of claims
Form each falls within protection scope of the present invention.
Claims (11)
1. a kind of oriented electrical steel comprising base steel sheet, relative to the 100 weight % of total component of the base steel sheet, institute
Stating base steel sheet includes Si:1.0 weight % to 7.0 weight %, C:0.0050 weight % or less and do not include 0 weight %, Al:
0.005 weight % or less and do not include 0 weight %, N:0.0055 weight % or less and do not include 0 weight %, S:0.0055 weight
It measures % or less and does not include 0 weight %, Mn:0.01 weight % to 0.5 weight %, and
Ba individually includes that 0.005 weight % to 0.5 weight % or Ba and Y jointly comprises 0.005 weight % to 0.5 weight %,
Surplus is Fe and impurity.
2. oriented electrical steel according to claim 1, wherein
Relative to total chip area 100%, the area ratio of the crystal grain with 2mm or less partial size is 10% or less.
3. oriented electrical steel according to claim 2, wherein
The average grain diameter of crystal grain with 2mm or more partial size is 10mm or more.
4. oriented electrical steel according to claim 3, wherein
<100>it is 3.5 ° or less that the plate face of face and steel plate, which is formed by differential seat angle,.
5. oriented electrical steel according to claim 4, wherein
The magnetic flux density B measured under the magnetic field of 1000A/m10It is 1.88 or more.
6. oriented electrical steel as claimed in any of claims 1 to 5, Ba or Ba and Y comprising segregating to crystal boundary
Combination.
7. a kind of manufacturing method of oriented electrical steel, includes the following steps:
Slab is heated, wherein relative to the total 100 weight % of component of the slab, the slab includes Si:1.0 weight
Measure % to 4.5 weight %, C:0.001 weight % to 0.1 weight %, Al:0.005 weight % or less, N:0.0055 weight % with
Under, S:0.0055 weight % or less, Mn:0.01 weight % to 0.5 weight % and Ba individually include 0.005 weight % to 0.5
Weight % or Ba and Y jointly comprises 0.005 weight % to 0.5 weight %, and surplus is Fe and other inevitable impurity；
Hot rolling is carried out to manufacture hot rolled plate to the slab；
Cold rolling is carried out to manufacture cold-reduced sheet to the hot rolled plate；
1 recrystallization annealing is carried out to the cold-reduced sheet；And
2 recrystallization annealing is carried out to the electric steel plate that 1 recrystallization annealing finishes.
8. the manufacturing method of oriented electrical steel according to claim 7, wherein
To in described the step of heating to slab, slab heating temperature is 1280 DEG C or less.
9. the manufacturing method of oriented electrical steel according to claim 8, wherein
Soaking temperature is 900 DEG C to 1250 DEG C when 2 recrystallization annealing.
10. the manufacturing method of oriented electrical steel according to claim 9, wherein
After the hot-rolled step, further include the steps that implementing hot rolled plate annealing.
11. the manufacturing method of oriented electrical steel according to claim 10, wherein
In 1 recrystallization annealing, by cold-reduced sheet 750 DEG C or more at a temperature of kept for 30 seconds or more.
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| KR10-2014-0180687 | 2014-12-15 | ||
| KR1020140180687A KR101647655B1 (en) | 2014-12-15 | 2014-12-15 | Grain orientied electrical steel sheet and method for manufacturing the same |
| PCT/KR2014/012409 WO2016098917A1 (en) | 2014-12-15 | 2014-12-16 | Grain-oriented electrical steel sheet and manufacturing method therefor |
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| JP (2) | JP6559784B2 (en) |
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| KR102177523B1 (en) | 2015-12-22 | 2020-11-11 | 주식회사 포스코 | Grain orientied electrical steel sheet and method for manufacturing the same |
| JP6572855B2 (en) | 2016-09-21 | 2019-09-11 | Ｊｆｅスチール株式会社 | Oriented electrical steel sheet and manufacturing method thereof |
| KR101884428B1 (en) * | 2016-10-26 | 2018-08-01 | 주식회사 포스코 | Grain oriented electrical steel sheet and method for manufacturing the same |
| KR101869455B1 (en) * | 2016-12-19 | 2018-06-20 | 주식회사 포스코 | Grain oriented electrical steel sheet and method for manufacturing the same |
| KR101966370B1 (en) * | 2016-12-21 | 2019-04-05 | 주식회사 포스코 | Method for manufacturing grain oriented electrical steel sheet |
| KR101947026B1 (en) * | 2016-12-22 | 2019-02-12 | 주식회사 포스코 | Grain oriented electrical steel sheet and method for manufacturing the same |
| KR101919521B1 (en) | 2016-12-22 | 2018-11-16 | 주식회사 포스코 | Grain oriented electrical steel sheet and method for manufacturing the same |
| WO2018207873A1 (en) * | 2017-05-12 | 2018-11-15 | Ｊｆｅスチール株式会社 | Oriented magnetic steel sheet and method for manufacturing same |
| KR102437377B1 (en) | 2017-12-28 | 2022-08-26 | 제이에프이 스틸 가부시키가이샤 | Low iron loss grain-oriented electrical steel sheet and manufacturing method thereof |
| KR102176348B1 (en) * | 2018-11-30 | 2020-11-09 | 주식회사 포스코 | Grain oriented electrical steel sheet and manufacturing method of the same |
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| EP3235919A1 (en) | 2017-10-25 |
| WO2016098917A1 (en) | 2016-06-23 |
| KR101647655B1 (en) | 2016-08-11 |
| EP3235919A4 (en) | 2017-12-06 |
| US20170335425A1 (en) | 2017-11-23 |
| EP3235919B1 (en) | 2019-09-25 |
| EP3235919B9 (en) | 2019-12-25 |
| JP2019148009A (en) | 2019-09-05 |
| JP2018505961A (en) | 2018-03-01 |
| US10760141B2 (en) | 2020-09-01 |
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| CN107002204A (en) | 2017-08-01 |
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